U.S. patent application number 13/327262 was filed with the patent office on 2012-07-05 for ni and cu free pd-based metallic glasses.
This patent application is currently assigned to California Institute of Technology. Invention is credited to Marios D. Demetriou, William L. Johnson.
Application Number | 20120168037 13/327262 |
Document ID | / |
Family ID | 46379683 |
Filed Date | 2012-07-05 |
United States Patent
Application |
20120168037 |
Kind Code |
A1 |
Demetriou; Marios D. ; et
al. |
July 5, 2012 |
NI AND CU FREE PD-BASED METALLIC GLASSES
Abstract
The invention is directed to Pd-based metallic glass alloys
useful in biomedical applications having no Ni or Cu. Exemplary
metallic glass alloys are represented by
A.sub.aB.sub.b{(Si).sub.100-c(D).sub.c}.sub.d, where A may be
selected from Pd, and combinations of Pd and Pt, B may be selected
from Ag, Au, Co, Fe, and combinations thereof, and D may be
selected from P, Ge, B, S. Also, a, b, c and d are atomic
percentages, and a ranges from about 60 to about 90, b ranges from
about 2 to about 18, d ranges from about 5 to about 25, and c is
greater than 0 and less than 100.
Inventors: |
Demetriou; Marios D.; (Los
Angeles, CA) ; Johnson; William L.; (San Marino,
CA) |
Assignee: |
California Institute of
Technology
Pasadena
CA
|
Family ID: |
46379683 |
Appl. No.: |
13/327262 |
Filed: |
December 15, 2011 |
Related U.S. Patent Documents
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Application
Number |
Filing Date |
Patent Number |
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13306311 |
Nov 29, 2011 |
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13327262 |
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12172908 |
Jul 14, 2008 |
8066827 |
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13306311 |
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60959296 |
Jul 12, 2007 |
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61423304 |
Dec 15, 2010 |
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Current U.S.
Class: |
148/403 |
Current CPC
Class: |
C22C 45/003
20130101 |
Class at
Publication: |
148/403 |
International
Class: |
C22C 45/00 20060101
C22C045/00 |
Claims
1. A metallic glass comprising a biocompatible alloy represented by
Formula 1: Pd.sub.aX.sub.bSi.sub.cP.sub.dGe.sub.e (1) wherein: X is
Ag, Au, or a combination of Ag and Au, a is an atomic percent
ranging from about 74 to about 86, b is an atomic percent ranging
from about 2 to about 5, c is an atomic percent ranging from about
8 to about 10, d is an atomic percent ranging from about 4 to about
8, and e is an atomic percent ranging from about 0 to about 3.
2. The metallic glass of claim 1, wherein a is between 78.5 and
81.5, b is between 2.75 and 4.25, c is between 8.75 and 9.75, d is
between 5 and 7, and e is between 1.5 and 2.5.
3. The metallic glass of claim 1, wherein X is Ag.
4. The metallic glass of claim 1, wherein the alloy is selected
from the group consisting of
Pd.sub.78.5Ag.sub.5Si.sub.85P.sub.6Ge.sub.2,
Pd.sub.79Ag.sub.4.5Si.sub.8.5P.sub.6Ge.sub.2,
Pd.sub.79.5Ag.sub.4Si.sub.8.5P.sub.6Ge.sub.2,
Pd.sub.80Ag.sub.3.5Si.sub.8.5P.sub.6Ge.sub.2,
Pd.sub.80.5Ag.sub.3Si.sub.8.5P.sub.6Ge.sub.2,
Pd.sub.81Ag.sub.2.5Si.sub.8.5P.sub.6Ge.sub.2,
Pd.sub.79Ag.sub.3Si.sub.10P.sub.6Ge.sub.2,
Pd.sub.80Ag.sub.3Si.sub.9P.sub.6Ge.sub.2,
Pd.sub.79Ag.sub.4Si.sub.9P.sub.6Ge.sub.2,
Pd.sub.79.5Ag.sub.3.5Si.sub.9P.sub.6Ge.sub.2,
Pd.sub.79.5Ag.sub.3Si.sub.9.5P.sub.6Ge.sub.2, and
Pd.sub.79Ag.sub.3.5Si.sub.9.5P.sub.6Ge.sub.2.
5. A three-dimensional object formed of a metallic glass comprising
a biocompatible alloy represented by Formula 1:
Pd.sub.a,X.sub.bSi.sub.cP.sub.dGe.sub.e (1) wherein: X is Ag, Au,
or a combination of Ag and Au, a is an atomic percent ranging from
about 74 to about 86, b is an atomic percent ranging from about 2
to about 5, c is an atomic percent ranging from about 8 to about
10, d is an atomic percent ranging from about 4 to about 8, and e
is an atomic percent ranging from about 0 to about 3.
6. The three dimensional object of claim 5, wherein the
three-dimensional object has a critical casting thickness greater
than about 3 mm.
7. The three-dimensional object of claim 5, wherein the
three-dimensional object has a critical casting thickness ranging
from about 3 mm to about 6 mm.
8. The three-dimensional object of claim 5, wherein the
three-dimensional object has a critical casting thickness ranging
of greater than 6 mm.
9. The three-dimensional object of claim 5, wherein the
three-dimensional object is a biomedical component.
10. The three-dimensional object of claim 9, wherein the biomedical
component is a dental or orthodontic component.
11. The three-dimensional object of claim 9, wherein the biomedical
component is an orthopedic component.
12. The three-dimensional object of claim 9, wherein the biomedical
component is an implant or fixation device.
13. The three-dimensional object of claim 9, wherein the biomedical
component is an orthodontic bracket or wire.
14. The three-dimensional object of claim 5, wherein the
three-dimensional object is a jewelry article.
15. The three-dimensional object of claim 5, wherein the
three-dimensional object is a watch component or device.
16. The three-dimensional object of claim 5, wherein a is between
78.5 and 81.5, b is between 2.75 and 4.25, c is between 8.75 and
9.75, d is between 5 and 7, and e is between 1.5 and 2.5.
17. The three-dimensional object of claim 5, wherein X is Ag.
18. The three-dimensional object of claim 5, wherein the
biocompatible alloy is selected from the group consisting of
Pd.sub.78.5Ag.sub.5Si.sub.8.5P.sub.6Ge.sub.2,
Pd.sub.79Ag.sub.4.5Si.sub.8.5P.sub.6Ge.sub.2,
Pd.sub.79.5Ag.sub.4Si.sub.8.5P.sub.6Ge.sub.2,
Pd.sub.80Ag.sub.3.5Si.sub.8.5P.sub.6Ge.sub.2,
Pd.sub.80.5Ag.sub.3Si.sub.8.5P.sub.6Ge.sub.2,
Pd.sub.81Ag.sub.2.5Si.sub.8.5P.sub.6Ge.sub.2,
Pd.sub.79Ag.sub.3Si.sub.10P.sub.6Ge.sub.2,
Pd.sub.80Ag.sub.3Si.sub.9P.sub.6Ge.sub.2,
Pd.sub.79Ag.sub.4Si.sub.9P.sub.6Ge.sub.2,
Pd.sub.79.5Ag.sub.3.5Si.sub.9P.sub.6Ge.sub.2,
Pd.sub.79.5Ag.sub.3Si.sub.9.5P.sub.6Ge.sub.2, and
Pd.sub.79Ag.sub.3.5Si.sub.9.5P.sub.6Ge.sub.2.
Description
CROSS-REFERENCE TO RELATED APPLICATION(S)
[0001] This application is a continuation-in-part of U.S. patent
application Ser. No. 13/306,311, filed Nov. 29, 2011, which is a
continuation of U.S. patent application Ser. No. 12/172,908, filed
Jul. 14, 2008, which claims priority to and the benefit of
Provisional Application Ser. No. 60/959,296, filed on Jul. 12, 2007
and entitled NI AND CU FREE PD-BASED GLASSES, the application also
claims priority to U.S. Provisional No. 61/423,304, filed Dec. 15,
2010, the entire content of each of which are incorporated herein
by reference.
FIELD OF THE INVENTION
[0002] The invention is directed to Ni and Cu free Pd-based
metallic glasses. More particularly, the invention is directed to
Pd-based glass-forming alloys useful in biomedical
applications.
BACKGROUND OF THE INVENTION
[0003] Metallic glasses, unlike conventional crystalline alloys,
have amorphous or disordered atomic-scale structures that give rise
to unique chemical, mechanical, and rheological properties. Owing
to their atomic structure, metallic glasses generally exhibit
better corrosion resistance than typical crystalline alloys, higher
hardness, strength, and elasticity, and are able to soften and flow
when relaxed above their glass transition temperatures (T.sub.g), a
characteristic that allows for considerable processing capability.
Previously, metallic glasses were only capable of being produced in
sub-millimeter dimensions (thin ribbons, sheets, wires, or powders)
due to the need for rapid cooling from the liquid state to avoid
crystallization. However, recent developments in bulk glass-forming
alloys have enabled the production of metallic systems with very
sluggish crystallization kinetics able to form glasses in
dimensions as large as several centimeters. These developments have
permitted the introduction of metallic glasses in many engineering
applications where their unique chemical and mechanical properties,
including good corrosion resistance, high strength and hardness,
and large elastic elongation, are desirable.
[0004] The most robust glass-forming metallic system to date is a
Pd--Ni--Cu--P alloy, which is capable of forming amorphous parts
with thicknesses as large as seven centimeters. The ability to
produce metallic glass ingots of such increased thickness has
aroused interest in many applications. However, due to the
prohibitively high cost of Pd (a noble metal) most of these
applications remain out of reach. Applications for which the high
cost of noble metals (such as Pd) is not considered as prohibitive
include jewelry and watches and biomedical applications (such as
orthopedic and dental/orthodontic applications). Interestingly, the
noble-metal character of Pd makes Pd-based glasses particularly
attractive for such applications. However, the only Pd-based
metallic glasses known to achieve dimensions of a few millimeters
or more contain either or both Ni and Cu in the alloy composition.
Indeed, the glass-forming ability of metals in general is widely
known and recognized to be heavily dependent on the inclusion of Ni
and/or Cu in the alloy, and it is the inclusion of these metals
that enabled the development of such robust metallic glass formers.
As such, the inclusion of Ni and Cu is widely accepted as necessary
to the formation of glass-forming alloys, and skilled artisans in
the field would have no expectation of success in creating a good
glass-forming alloy without including at least one of these
metals.
[0005] While the inclusion of Ni and Cu in metallic glasses is
generally suitable and acceptable when the glasses are used for
engineering applications, these metals are highly cytotoxic, making
metallic glasses including these metals ill suited for biomedical
applications. In particular, Ni and Cu are highly electronegative,
allowing them to exist as free radicals in the blood stream. Such
free radicals are notorious triggers for severe adverse biological
reactions in the body. Consequently, Ni and Cu are widely
understood and regarded as non-biocompatible, and any metallic
glasses including these metals are similarly understood to be
non-biocompatible. As the glass-forming ability of amorphous metal
alloys is strongly dependent on the inclusion of Ni and/or Cu,
development of Pd-based metallic glasses suitable for use in
biomedical applications has proved extremely challenging, and no
suitable such metallic glass has yet been achieved.
SUMMARY OF THE INVENTION
[0006] In some embodiments, the invention is directed to metallic
glass alloys represented by Formula 1.
A.sub.aB.sub.b{(Si).sub.100-c(D).sub.c}.sub.d (1)
In Formula 1, A may be Pd, or a combination of Pd and Pt, B may be
selected from Ag, Au, Co, Fe, and combinations thereof, and D may
be selected from P, Ge, B, S. Also, a, b, c and d are atomic
percentages, and a ranges from about 60 to about 90, b ranges from
about 2 to about 18, d ranges from about 5 to about 25, and c is
greater than 0 and less than 100.
[0007] In other embodiments, the invention is directed to metallic
glass alloys represented by Formula 2.
Pd.sub.aX.sub.bSi.sub.cP.sub.dGe.sub.e (2)
where X is one of either Ag or Au, or combination thereof, and
where the subscripts denote atomic percent and having the following
limits: a is between 74 and 86, preferably between 78.5 and 81.5,
and more preferably 79; b is between 2 and 5, preferably between
2.75 and 4.25, and more preferably 3.5; c is between 8 and 10,
preferably between 8.75 and 9.75, and more preferably 9.5; d is
between 4 and 8, preferably between 5 and 7, and more preferably 6;
and e is between 0 and 3, preferably 1.5 and 2.5, and more
preferably 2.
[0008] In other embodiments of the invention, three-dimensional
objects are formed from the alloys represented by Formulas 1 and 2.
The three-dimensional objects, e.g. rods, have diameters greater
than 3 mm and can have diameters as large as 6 mm. In some
embodiments, for example, the three-dimensional objects may be rods
with diameters ranging from greater than 1 mm to about 4 mm. In
other embodiments the three-dimensional objects may have dimensions
greater than 6 mm.
BRIEF DESCRIPTION OF THE DRAWINGS
[0009] These and other features and advantages of the present
invention will be better understood by reference to the following
detailed description when considered in conjunction with the
attached drawings, in which:
[0010] FIG. 1 is a photograph of a 1-mm glassy
Pd.sub.77.5Ag.sub.6Si.sub.9P.sub.7.5 wire produced as in Example 3
by the capillary water-quenching method.
[0011] FIG. 2 is a graph comparing the differential scanning
calorimetry scans of the alloys prepared according to Examples 2
and 15 and Comparative Example 1;
[0012] FIG. 3 is a graph of the X-ray diffractograms of the alloys
prepared according to Examples 1 through 3;
[0013] FIG. 4 is a graph comparing the differential scanning
calorimetry scans of the alloys prepared according to Examples 30
and 32 and Comparative Example 2;
[0014] FIG. 5 is an X-ray diffractogram of the alloy prepared
according to Examples 30;
[0015] FIG. 6 is an image of amorphous
Pd.sub.79Ag.sub.3.5P.sub.6Si.sub.9.5Ge.sub.2 rods with diameters
ranging between 3 and 6 mm;
[0016] FIG. 7 is a data plot of a differential scanning calorimetry
study of an amorphous Pd.sub.79Ag.sub.3.5P.sub.6Si.sub.9.5Ge.sub.2
sample (arrows from left to right indicate the glass-transition
temperature T.sub.g=337.degree. C., the crystallization temperature
T.sub.x=370.degree. C., the solidus temperature T.sub.s=691.degree.
C., and the liquidus temperature T.sub.l=793.degree. C.);
[0017] FIG. 8 is a data plot of an X-ray diffraction analysis of
amorphous Pd.sub.79Ag.sub.3.5P.sub.6Si.sub.9.5Ge.sub.2 rods with
diameters ranging between 3 and 6 mm;
[0018] FIG. 9 is graph of the compressive stress-strain response of
a glassy Pd.sub.77.5Ag.sub.6Si.sub.9P.sub.7.5 specimen prepared as
in Example 3; and
[0019] FIG. 10 is a photograph of a bent glassy
Pd.sub.77.5Ag.sub.6Si.sub.9P.sub.7.5 wire of variable thickness
produced as in Example 3 by the capillary water-quenching
method.
DETAILED DESCRIPTION OF THE INVENTION
[0020] To form metallic glasses useful in biomedical applications,
the glass-forming alloys should be biocompatible and able to form
glassy parts at sufficiently large dimensions (greater than 1 mm)
to manufacture the desired biomedical components. Moreover, the
glasses should have low Young's modulus and high toughness
characteristics. Metallic glasses with these characteristics would
be especially useful in biomedical applications such as orthopedic
and orthodontic implants and fixation components (wires, nails,
plates, screws, etc).
[0021] Although Pd-based metallic glasses generally have the
required modulus and toughness characteristics and are able to form
three-dimensional metallic glass objects of sufficient thickness
for biomedical applications, these metallic glasses include at
least one of Ni and Cu (and often both), likely making them
non-biocompatible and therefore ill suited for use in biomedical
applications. However, because Pd-based metallic glasses have
desirable modulus and toughness characteristics, the present
invention is directed to Pd-based metallic glasses free of Ni and
Cu.
[0022] In addition to biomedical applications, the inventive alloys
that are free of Ni and Cu can be useful in jewelry articles and
watches. As Ni and Cu are known to produce allergic reactions in
many individuals, the inventive alloys, excluding these metals, are
particularly suitable for use in jewelry and watch
applications.
[0023] In some embodiments of the present invention, a metallic
glass includes a biocompatible alloy represented by Formula 1.
A.sub.aB.sub.b{(Si).sub.100-c(D).sub.c}.sub.d (1)
In Formula 1, A may be Pd, or a combination of Pd and Pt, B may be
selected from Ag, Au, Co, Fe, and combinations thereof, and D may
be selected from P, Ge, B, S, and combinations thereof. Also, a, b,
c and d are atomic percentages, and a ranges from about 60 to about
90, b ranges from about 2 to about 18, d ranges from about 5 to
about 25, and c is greater than 0 and less than 100. In one
embodiment, B is selected from Au, Ag and combinations thereof. In
another embodiment, D is selected from P, Ge, and combinations
thereof.
[0024] Nonlimiting examples of suitable alloys satisfying Formula 1
include Pd.sub.77.5Ag.sub.6Si.sub.14P.sub.2.5,
Pd.sub.77.5Ag.sub.6Si.sub.11.5P.sub.5,
Pd.sub.77.5Ag.sub.6Si.sub.9P.sub.7.5,
Pd.sub.77.5Ag.sub.6Si.sub.6.5P.sub.10,
Pd.sub.77.5Ag.sub.6Si.sub.4P.sub.12.55
Pd.sub.79.5Ag.sub.4Si.sub.9P.sub.7.5,
Pd.sub.78.5Ag.sub.5Si.sub.11.5P.sub.5,
Pd.sub.76.5Ag.sub.7Si.sub.11.5P.sub.5,
Pd.sub.75.5Ag.sub.8Si.sub.9P.sub.7.5,
Pd.sub.75.5Ag.sub.8Si.sub.11.5P.sub.5,
Pd.sub.75Ag.sub.8.5Si.sub.11.5P.sub.5,
Pd.sub.73.5Ag.sub.10Si.sub.11.5P.sub.5,
Pd.sub.76.85Ag.sub.8.14Si.sub.10.45P.sub.4.55,
Pd.sub.74.14Ag.sub.7.86Si.sub.12.55P.sub.5.45,
Pd.sub.75.5Ag.sub.8Si.sub.9Ge.sub.2.5P.sub.5,
Pd.sub.75.5Ag.sub.8Si.sub.9.5Ge.sub.2P.sub.5,
Pd.sub.75Ag.sub.8.5Si.sub.9.5Ge.sub.2P.sub.5,
Pd.sub.76Ag.sub.7.5Si.sub.9.5Ge.sub.2P.sub.5,
Pd.sub.75.5Ag.sub.8Si.sub.10.5Ge.sub.2P.sub.4,
Pd.sub.75.5Ag.sub.8Si.sub.8.5Ge.sub.2P.sub.6,
Pd.sub.75.5Ag.sub.8Si.sub.6.5Ge.sub.5P.sub.5,
Pd.sub.75.5Ag.sub.8Si.sub.4Ge.sub.7.5P.sub.5,
Pd.sub.75.5Ag.sub.8Si.sub.2.5Ge.sub.9P.sub.5,
Pd.sub.73Ag.sub.8Ge.sub.14P.sub.5,
Pd.sub.75.5Ag.sub.8Ge.sub.11.5P.sub.5,
Pd.sub.77Ag.sub.8Ge.sub.10P.sub.5,
Pd.sub.75.5Ag.sub.8Si.sub.9P.sub.5S.sub.2.5,
Pd.sub.75.5Ag.sub.8Si.sub.2.5Ge.sub.7P.sub.5S.sub.2,
Pd.sub.79Au.sub.4Si.sub.12P.sub.5,
Pd.sub.79Au.sub.4Si.sub.12Ge.sub.5,
Pd.sub.79Au.sub.4Si.sub.9.5Ge.sub.2.5P.sub.5, and
Pd.sub.75.5Ag.sub.8Si.sub.2.5Ge.sub.7P.sub.5S.sub.2.
[0025] As denoted in Formula 1 and the exemplary alloys listed
above, the Si in the alloy is fractionally substituted with an
element selected from P, Ge, B, S and combinations thereof. This
fractional substitution of the Si in the alloy improves the glass
forming ability by reducing the critical cooling rate needed to
bypass crystallization, thereby increasing the achievable size of
three-dimensional objects made from the amorphous alloys. Also, the
fractional substitution of Si could improve the thermoplastic
processability of the amorphous alloy by increasing the temperature
range between the glass transition and crystallization, thereby
increasing the window of processability in the supercooled liquid
region. In addition, the Si substitution in the alloy could also
improve the mechanical properties of the alloy by reducing shear
modulus and increasing Poisson's ratio, thereby improving fracture
toughness and ductility.
[0026] In some embodiments, the alloy represented by Formula 1 may
include additional alloying elements in atomic percentages that are
within the impurity level of about 2%.
[0027] One exemplary method for producing an alloy represented by
Formula 1 involves inductively melting an appropriate amount of the
alloy constituents in a quartz tube under an inert atmosphere.
However, for alloys containing high concentrations of P, a P-free
pre-alloy is first produced by melting appropriate amount of the
alloy constituents (except for P) in a quartz tube under an inert
atmosphere, and then adding P by enclosing it with the pre-alloy in
a quartz tube sealed under an inert atmosphere. The sealed tube is
then placed in a furnace and the temperature is increased
intermittently.
[0028] According to another embodiment of the present invention,
the alloys represented by Formula 1 may be formed into
three-dimensional objects useful in many applications. In addition
to engineering and mechanical applications, because the metallic
glasses of the present invention are free of elements known to
cause adverse biological reactions (such as Ni and Cu),
three-dimensional objects made from the alloys would be
biocompatible and therefore useful in many biomedical applications.
For example, the three-dimensional objects may be useful as
orthopedic and/or orthodontic implants and fixation components such
as wires, nails, plates or screws.
[0029] The alloys according to the present invention may be used to
form three-dimensional bulk objects, e.g. rods, having diameters
greater than about 1 mm. FIG. 1 is a photograph of a glassy 1-mm
Pd.sub.77.5Ag.sub.6Si.sub.9P.sub.7.5 produced as in Example 3 using
the capillary water-quenching method described below. In
particular, the alloys can be used to form three-dimensional
objects having diameters up to about 5 mm. In many embodiments, for
example, the alloys produce three-dimensional objects having
diameters ranging from 2 to 4 mm. Because Ni and Cu are generally
considered essential in any alloy for achieving three-dimensional
objects with such bulk diameters, the ability of the alloys
according to embodiments of the present invention, which are free
of Ni and Cu, to form objects with these diameters is particularly
surprising.
[0030] An exemplary method of producing three-dimensional bulk
objects having at least 50% (by volume) amorphous phase involves
first inductively melting the alloy in contact with a piece of
molten de-hydrated B.sub.2O.sub.3 in a quartz tube under an inert
atmosphere. The entire alloy, while still in contact with the
molten de-hydrated B.sub.2O.sub.3, is then cooled from above its
melting temperature to a temperature below its glass transition
temperature at a rate sufficient to prevent the formation of more
than 50% crystalline phase.
[0031] The following examples are presented for illustrative
purposes only and do not limit the scope of the present invention.
In the examples, the alloys were prepared by the capillary
water-quenching method using elements with purities of about 99.9%
or greater. In particular, the elements were weighed to within
about 0.1% of the calculated mass, and were ultrasonically cleaned
in acetone and ethanol prior to melting. Melting of the elements
was performed inductively in quartz tubes sealed under a partial
atmosphere of argon. The alloyed ingots were subsequently fluxed
with dehydrated B.sub.2O.sub.3. Fluxing was performed by
inductively melting the ingots together with dehydrated
B.sub.2O.sub.3 in quartz tubes under argon, holding the melted
ingots at a temperature roughly 50 degrees above the alloy melting
point for approximately 15 minutes, and finally water quenching the
ingots. The fluxed ingots were cast into glassy rods using quartz
capillaries. The ingots were placed into quartz tubes attached on
the capillaries, melted in a furnace under vacuum, injected into
the capillaries using 1.5 atmospheres of argon, and finally water
quenched. The amorphous nature of the glassy rods was verified
using at least one of the following methods: (a) x-ray diffraction
(verification of the amorphous state if the diffraction pattern
exhibits no crystalline peaks); (b) differential scanning
calorimetry (verification of the amorphous state if the scan
reveals a glass transition event followed by a crystallization
event upon heating from room temperature); (c) microscopic
inspection of rod failure characteristics (verification of the
amorphous phase if plastically deformed regions reveal shear band
networks, and fracture surfaces exhibit sharply defined shiny
facets). The compositions of each of the Examples and Comparative
Examples are listed in Tables 1 and 2.
[0032] Glass formation is a result of rapidly cooling the material,
causing it to bypass the formation of stable crystal configurations
and consequently freeze-in a liquid-like atomic configuration (i.e.
a glassy state). A relatively good glass former is an alloy that
requires relatively low cooling rate to form the glassy state, or
alternatively, is capable of forming relatively thick glassy
sections for a given cooling rate. The glass forming ability of
alloys is therefore quantified in terms of the alloy limiting part
dimension that can turn glassy when cooled at a certain
heat-removal rate, which is termed the "critical casting
thickness". Since the exemplary alloys were quenched in quartz
capillaries whose inner diameters and wall thicknesses varied, and
since quartz is known to be a poor heat conductor that retards heat
transfer, the quartz-capillary wall thickness should also be a
factor in determining glass-forming ability of the exemplary
alloys. The glass-forming ability of the various exemplary alloys
is hence determined by the maximum rod diameter that can be formed
glassy based on a given capillary wall thickness. The critical rod
diameters and the associated capillary wall thicknesses are
tabulated for some exemplary alloys in Table 1, and thermodynamic
properties are reported in Table 2. In Table 1, DSC means
differential scanning calorimetry, XRD means X-ray diffraction, and
INSP means microscopic inspection. In Table 2, T.sub.g is the glass
transition temperature, T.sub.x is the crystallization temperature,
.DELTA.H.sub.x is the enthalpy of crystallization, T.sub.s is the
solidus temperature, T.sub.l is the liquidus temperature, and
.DELTA.H.sub.m is the enthalpy of melting. In Table 2, the ratio of
T.sub.g over T.sub.s, which is termed the "reduced glass
transition", is given in absolute Kelvin units.
TABLE-US-00001 TABLE 1 Quartz Verification Example Alloy
composition Rod Diameter Thickness Method Comparative
Pd.sub.77.5Ag.sub.6Si.sub.16.5 1.1 mm 0.11 mm DSC Example 1 1
Pd.sub.77.5Ag.sub.6Si.sub.14P.sub.2.5 1.4 mm 0.14 mm DSC, XRD 2
Pd.sub.77.5Ag.sub.6Si.sub.11.5P.sub.5 2.5 mm 0.25 mm DSC, XRD 3
Pd.sub.77.5Ag.sub.6Si.sub.9P.sub.7.5 3.0 mm 0.15 mm DSC, XRD 4
Pd.sub.77.5Ag.sub.6Si.sub.6.5P.sub.10 1.5 mm 0.15 mm DSC, XRD 5
Pd.sub.77.5Ag.sub.6Si.sub.4P.sub.12.5 1.0 mm 0.10 mm DSC, XRD 6
Pd.sub.78.5Ag.sub.5Si.sub.11.5P.sub.5 2.2 mm 0.22 mm INSP 7
Pd.sub.76.5Ag.sub.7Si.sub.11.5P.sub.5 2.4 mm 0.24 mm INSP 8
Pd.sub.75.5Ag.sub.8Si.sub.9P.sub.7.5 2.2 mm 0.22 mm INSP 9
Pd.sub.75.5Ag.sub.8Si.sub.11.5P.sub.5 2.7 mm 0.27 mm DSC, XRD 10
Pd.sub.75Ag.sub.8.5Si.sub.11.5P.sub.5 2.7 mm 0.27 mm DSC, XRD 11
Pd.sub.73.5Ag.sub.10Si.sub.11.5P.sub.5 1.7 mm 0.17 mm INSP 12
Pd.sub.76.85Ag.sub.8.14Si.sub.10.45P.sub.4.55 1.5 mm 0.15 mm INSP
13 Pd.sub.74.14Ag.sub.7.86Si.sub.12.55P.sub.5.45 2.2 mm 0.22 mm
INSP 14 Pd.sub.75.5Ag.sub.8Si.sub.9Ge.sub.2.5P.sub.5 2.8 mm 0.28 mm
DSC, XRD 2.0 mm 0.5 mm DSC 3.0 mm 0.15 mm DSC 15
Pd.sub.75.5Ag.sub.8Si.sub.9.5Ge.sub.2P.sub.5 2.5 mm 0.36 mm INSP 16
Pd.sub.75Ag.sub.8.5Si.sub.9.5Ge.sub.2P.sub.5 2.2 mm 0.31 mm INSP 18
Pd.sub.76Ag.sub.7.5Si.sub.9.5Ge.sub.2P.sub.5 2.3 mm 0.33 mm INSP 19
Pd.sub.75.5Ag.sub.8Si.sub.10.5Ge.sub.2P.sub.4 1.5 mm 0.21 mm INSP
20 Pd.sub.75.5Ag.sub.8Si.sub.8.5Ge.sub.2P.sub.6 2.5 mm 0.36 mm INSP
21 Pd.sub.75.5Ag.sub.8Si.sub.6.5Ge.sub.5P.sub.5 1.0 mm (P/A) 0.10
mm (P/A) DSC, XRD (Partially amorphous) 22
Pd.sub.75.5Ag.sub.8Si.sub.4Ge.sub.7.5P.sub.5 2.4 mm 0.24 mm DSC 23
Pd.sub.75.5Ag.sub.8Si.sub.2.5Ge.sub.9P.sub.5 1.5 mm 0.15 mm DSC 24
Pd.sub.74Ag.sub.7Si.sub.5Ge.sub.9P.sub.5 1.5 mm 0.15 mm INSP 25
Pd.sub.73Ag.sub.8Ge.sub.14P.sub.5 1.0 mm 0.10 mm DSC 26
Pd.sub.75.5Ag.sub.8Ge.sub.11.5P.sub.5 1.0 mm (P/A) 0.10 mm (P/A)
DSC (Partially amorphous) 27 Pd.sub.77Ag.sub.8Ge.sub.10P.sub.5 1.0
mm (P/A) 0.10 mm (P/A) DSC (Partially amorphous) 28
Pd.sub.75.5Ag.sub.8Si.sub.9P.sub.5S.sub.2.5 1.0 mm (P/A) 0.10 mm
(P/A) DSC, XRD (Partially amorphous) 29
Pd.sub.75.5Ag.sub.8Si.sub.2.5Ge.sub.7P.sub.5S.sub.2 1.0 mm 0.10 mm
DSC Comparative Pd.sub.79Au.sub.4Si.sub.17 -- -- DSC (not Example 2
amorphous) 30 Pd.sub.79Au.sub.4Si.sub.12P.sub.5 2.2 mm 0.22 mm DSC,
XRD 31 Pd.sub.79Au.sub.4Si.sub.12Ge.sub.5 1.0 mm 0.10 mm DSC, XRD
(partially amorphous) 32
Pd.sub.79Au.sub.4Si.sub.9.5Ge.sub.2.5P.sub.5 1.6 mm 0.16 mm DSC
TABLE-US-00002 TABLE 2 T.sub.g T.sub.x .DELTA.H.sub.x T.sub.s
T.sub.l T.sub.g/T.sub.s .DELTA.H.sub.m Example Composition
[.degree. C.] [.degree. C.] [J/g] [.degree. C.] [.degree. C.] (K/K)
[J/g] Comparative. Pd.sub.77.5Ag.sub.6Si.sub.16.5 354 403 -29 787
809 0.59 95 Example 1 2 Pd.sub.77.5Ag.sub.6Si.sub.11.5P.sub.5 344
395 -29 710 773 0.63 89 3 Pd.sub.77.5Ag.sub.6Si.sub.9P.sub.7.5 338
401 -36 710 832 0.62 99 10 Pd.sub.75.5Ag.sub.8Si.sub.11.5P.sub.5
344 375 -34 709 796 0.63 84 15
Pd.sub.75.5Ag.sub.8Si.sub.9Ge.sub.2.5P.sub.5 341 370 -30 693 806
0.64 72 30 Pd.sub.79Au.sub.4Si.sub.12P.sub.5 344 383 -30 719 796
0.62 87 32 Pd.sub.79Au.sub.4Si.sub.9.5Ge.sub.2.5P.sub.5 336 370 -28
691 737 0.63 73
[0033] The amorphous nature of the compositions of the Examples and
Comparative Examples were investigated using at least one of X-ray
diffraction analysis, differential scanning calorimetry and
microscopic inspection. FIG. 2 compares the differential scanning
calorimetry scans of the compositions of Comparative Example 1 and
Examples 2 and 14. In FIG. 2, the glass transition and liquidus
temperatures for each alloy are indicated. FIG. 2 shows the X-ray
diffractograms of the compositions of Examples 1 through 3. As can
be seen in FIG. 3, no crystallographic peaks are detected in the
diffractograms, indicating the amorphous nature of the alloys. FIG.
4 compares the differential scanning calorimetry scans of the
compositions of Comparative Example 2 and Examples 30 and 32. In
FIG. 4, the glass transition and liquidus temperatures are
indicated, and as shown, no glass transition is detected for the
composition of Comparative Example 2. FIG. 5 shows the X-ray
diffractogram of the composition of Example 30. As can be seen in
FIG. 5, no crystallographic peaks are detected in the
diffractogram, thereby verifying the amorphous nature of the
alloy.
[0034] As shown in Tables 1 and 2 and FIGS. 2 through 5, the
compositions of Examples 1 through 32 are all amorphous or at least
partially amorphous, whereas the composition of Comparative Example
2 is not amorphous. Although the composition of Comparative Example
1 is amorphous, it can be seen from Table 2 that the composition of
Comparative Example 1 has a higher glass transition temperature and
solidus temperature. One of the earliest and most widely accepted
criteria for quantifying glass forming ability is based on a
comparative relation between the glass transition temperature and
the melting (solidus or liquidus) temperature (in absolute Kelvin
units). According to this criterion, the ratio of the glass
transition temperature (below which the liquid kinetically freezes)
to the melting temperature (below which the dominant crystalline
phase becomes thermodynamically stable), which is termed the
"reduced glass transition temperature," is a measure of the ease of
bypassing crystallization and forming the amorphous phase.
Therefore, according to this criterion, alloys with high reduced
glass transition temperatures will exhibit a greater glass forming
ability. As seen in Table 1, the introduction of P and Ge into the
composition of the Example alloys results in a slightly lower glass
transition temperature but also in a dramatically lower solidus
temperature with respect to the Comparative Examples. This results
in an overall higher reduced glass transition temperature (which is
shown to increase from 0.59 to as high as 0.64). This overall
increase in reduced glass transition temperature can, to a good
approximation, explain the improvement in glass forming ability
gained by the introduction of P and Ge into the compositions of the
Comparative Examples.
[0035] Although the above discussion has focussed on the broad
compositional limits described by Formula 1, it has now been
discovered that there is a particularly preferred compositional
range in which the glass-forming ability of the alloys is
maximized. Accordingly, in one preferred embodiment, optimal
glass-forming ability can be obtained by forming compositions
represented by Formula 2:
Pd.sub.aX.sub.bSi.sub.cP.sub.dGe.sub.e
where X is one of either Ag or Au, or combination thereof, and
where the subscripts denote atomic percent and having the following
limits:
[0036] a is between 74 and 86, preferably between 78.5 and 81.5,
and more preferably 79;
[0037] b is between 2 and 5, preferably between 2.75 and 4.25, and
more preferably 3.5;
[0038] c is between 8 and 10, preferably between 8.75 and 9.75, and
more preferably 9.5;
[0039] d is between 4 and 8, preferably between 5 and 7, and more
preferably 6; and
[0040] e is between 0 and 3, preferably 1.5 and 2.5, and more
preferably 2.
[0041] Compositions according to Formula 2, are found to form
glassy rods with diameters of greater than 3 mm and up to 6 mm or
more, when processed by water quenching the melt in quartz-tubes
with wall thickness of 0.5 mm. Exemplary alloys with compositions
that satisfy the disclosed composition Formula 2 were produced by
inductive melting of the appropriate amounts of elemental
constituents of 99.9% purity or better in a quartz tube under an
inert atmosphere. The alloyed ingots were then fluxed with
dehydrated boron oxide by re-melting the ingots in a quartz tube
under inert atmosphere, the alloy melt is then brought in contact
with the boron oxide melt and the two melts are allowed to interact
for approximately 1000 s, and subsequently water quenched. Glassy
rods were then formed from the alloys by re-melting the fluxed
alloy ingots in quartz tubes having 0.5-mm thick walls under inert
atmosphere and rapidly water quenching. Results from observations
of the properties of these alloys are presented in Table 3,
below.
TABLE-US-00003 TABLE 3 T.sub.g T.sub.x .DELTA.H.sub.x T.sub.s
T.sub.l .DELTA.H.sub.m D.sub.cr Example Composition [.degree. C.]
[.degree. C.] [J/g] [.degree. C.] [.degree. C.] [J/g] [mm] 1
Pd.sub.78.5Ag.sub.5Si.sub.8.5P.sub.6Ge.sub.2 334 362 -35 692 793 86
3 2 Pd.sub.79Ag.sub.4.5Si.sub.8.5P.sub.6Ge.sub.2 332 357 -34 692
793 85 3 3 Pd.sub.79.5Ag.sub.4Si.sub.8.5P.sub.6Ge.sub.2 330 356 -35
694 739 82 3 4 Pd.sub.80Ag.sub.3.5Si.sub.8.5P.sub.6Ge.sub.2 332 361
-37 689 721 88 3 5 Pd.sub.80.5Ag.sub.3Si.sub.8.5P.sub.6Ge.sub.2 330
363 -36 691 724 79 3 6 Pd.sub.81Ag.sub.2.5Si.sub.8.5P.sub.6Ge.sub.2
328 358 -33 698 731 81 3 7
Pd.sub.79Ag.sub.3Si.sub.10P.sub.6Ge.sub.2 339 397 -40 691 822 92 3
8 Pd.sub.80Ag.sub.3Si.sub.9P.sub.6Ge.sub.2 332 367 -37 690 751 83 4
9 Pd.sub.79Ag.sub.4Si.sub.9P.sub.6Ge.sub.2 332 364 -37 691 752 83 4
10 Pd.sub.79.5Ag.sub.3.5Si.sub.9P.sub.6Ge.sub.2 333 364 -36 691 754
83 5 11 Pd.sub.79.5Ag.sub.3Si.sub.9.5P.sub.6Ge.sub.2 334 374 -38
693 782 86 5 12 Pd.sub.79Ag.sub.3.5Si.sub.9.5P.sub.6Ge.sub.2 337
370 -38 691 793 85 6
[0042] The glass-forming ability of each alloy in Table 3 was
assessed by determining the maximum diameter of a rod that can be
formed amorphous when processed as described above. (It should be
noted that the alloy properties summarized in Tables 1 and 2,
above, were obtained using alloys that were processed by water
quenching the melt in quartz tubes having wall thicknesses between
0.1 and 0.5 mm.) The composition with the best glass froming
ability from the alloys of Table 1 and 2 is
Pd.sub.75.5Ag.sub.8Si.sub.9P.sub.5Ge.sub.2.5. This alloy was found
capable of forming amorphous rods with diameter up to 3 mm when
processed by water quenching the melt in a quartz tube with wall
thickness of 0.15 mm. But when processed in a quartz-tube with wall
thickness of 0.5 mm, the alloy could form amorphous rods with
diameters only up to 2 mm. The reason for this difference is that
the thicker quartz-tube wall substantially reduces the critical rod
diameter, because the very low thermal conductivity of the quartz
limits the heat removal rate.
[0043] The current alloys were processed by water quenching the
melt in a quartz tube having wall thickness of 0.5 mm, and were
found capable of forming amorphous rods wth diameters of at least 3
mm, and up to 6 mm or more. As shown in Table 3, the alloy
Pd.sub.79Ag.sub.3.5Si.sub.9.5P.sub.6Ge.sub.2 is capable of forming
amorphous rods of up to 6 mm in diameter or greater. An image
depicting amorphous Pd.sub.79Ag.sub.3.5Si.sub.9.5P.sub.6Ge.sub.2
rods with diameters ranging from 3 to 6 mm is presented in FIG. 6.
Differential scanning calorimetry and x-ray diffraction analyses
verifying the amorphous structure of bulk
Pd.sub.79Ag.sub.3.5Si.sub.9.5P.sub.6Ge.sub.2 are presented in FIGS.
7 and 8, respectively.
Investigation of Elastic and Mechanical Properties
[0044] The elastic constants of a glassy
Pd.sub.77.5Ag.sub.6Si.sub.9P.sub.7.5 cylindrical specimen (3 mm in
diameter, 6 mm in height) were measured ultrasonically by measuring
the shear and longitudinal wave-speeds using a pulse-echo overlap
set-up with 5-MHz piezoelectric transducers, and the density using
the Archimedes method. The shear modulus, bulk modulus, and Young's
modulus were measured to be 30 GPa, 169 GPa, and 85 GPa,
respectively, and the Poisson's ratio is found to be 0.42. The
compressive loading response of a glassy
Pd.sub.77.5Ag.sub.6Si.sub.9P.sub.7.5 cylindrical specimen (3 mm in
diameter, 6 mm in height) was investigated using a servo-hydraulic
Materials Testing System with a 50-kN load cell. A strain rate of
1.times.10.sup.-4 s.sup.-1 was applied. Strain was measured using a
linear variable differential transformer. The recorded
stress-strain response of this alloy is shown in FIG. 9, which
reveals a yield strength of about 1450 MPa, an elastic strain of
about 1.7%, and a plastic strain of about 2%.
[0045] The high yield strength and low Young's modulus suggest that
this class of alloys exhibit hardness, strength, and elasticity
that are considerably higher than typical crystalline engineering
metals and comparable to or higher than crystalline metallic
biomaterials. Moreover, the very high Poisson's ratio of these
alloys, which is in fact one of the highest measured for a metallic
glass, suggests that these alloys would exhibit high toughness. In
fact, bending of a glassy wire, as shown in FIG. 10, reveals that
the wire is able to plastically deform at diameters as high as 1.5
mm while bypassing fracture. The bending ductility at a 1.5 mm
section combined with a yield strength of about 1500 MPa indicate a
very high fracture toughness of roughly 100 MPa-m.sup.1/2. Since
high hardness, strength, elasticity, and toughness are all highly
desirable properties for the proper biomechanical functioning of
implant components, it is suggested that the present alloys can be
thought of as attractive alternatives to the present load-bearing
implant materials.
In Vitro Cytotoxicity Studies
[0046] The cytotoxicity of a glassy
Pd.sub.77.5Ag.sub.6Si.sub.9P.sub.7.5 test article was evaluated in
an in vitro biocompatibility study conducted by NAMSA (Northwood,
Ohio). The study was conducted to determine the potential for
cytotoxicity and was based on the International Organization for
Standardization 10993: Biological Evaluation of Medical Devices
Part 5: Test for Cytotoxicity: in vitro Methods guidelines.
[0047] A single extract of the test article was prepared using
single strength Minimum Essential Medium supplemented with 5% serum
and 2% antibiotics (1.times.MEM). In particular, a 3.1 g portion of
the test article was covered with 16 ml of 1.times.MEM, and a
single preparation was extracted with agitation at 37.degree. C.
for 24 hours. The test extract was placed onto three separate
monolayers of L-929 mouse fibroblast cells propagated in 5%
CO.sub.2. Three separate monolayers were prepared for the reagent
control, negative control and positive control. The reagent control
included a single aliquot of 1.times.MEM without any test material
and was subjected to the same extraction conditions as the test
article. A high density polyethylene was used as the negative
control. A single 30.8 cm.sup.2 portion of negative control
material was covered with 10 ml of 1.times.MEM and the preparation
was subjected to the same extraction conditions as the test
article. A tin stabilized polyvinylchloride was used as the
positive control. A single 60.8 cm.sup.2 portion of the positive
control material was covered with 20 ml of 1.times.MEM and
extracted with agitation at 37.degree. C. for 24 hours.
[0048] L-929 mouse fibroblast cells (ATCC CCL 1, NCTC Clone 929, of
strain L, or equivalent source) were propagated and maintained in
open wells containing 1.times.MEM in a gaseous environment of 5%
CO.sub.2. For this study 10 cm.sup.2 wells were seeded, labeled
with passage number and date, and incubated at 37.degree. C. in 5%
CO2 to obtain sub-confluent monolayers of cells prior to use.
Triplicate culture wells were selected which contained a
sub-confluent cell monolayer. The growth medium contained in
triplicate cultures was replaced with 2 ml of the test extract.
Similarly, triplicate cultures were replaced with 2 ml of the
reagent control, negative control, and positive control. All wells
were incubated at 37.degree. C. in the presence of 5% CO.sub.2 for
48 hours.
[0049] Following incubation, the cultures were examiner
microscopically (100.times.) to evaluate cellular characteristics
and percent lysis. The color of the test medium was also observed.
A color shift toward yellow was associated with an acidic pH range
and a color shift toward magenta to purple was associated with an
alkaline pH range. Each culture well was evaluated for percent
lysis and cell characteristics based on the rating scale presented
in Table 4.
TABLE-US-00004 TABLE 4 Grade Reactivity Conditions of all Cultures
0 None Discrete intracytoplasmic granules; no cell lysis 1 Slight
Not more than 20% of the cells are round, loosely attached, and
without intracytoplasmic granules; occasional lysed cells are
present 2 Mild Not more than 50% of the cells are round and devoid
of intracytoplasmic granules; no extensive cell lysis and empty
areas between cells 3 Moderate Not more than 70% of the cell layers
contain rounded cells or are lysed 4 Severe Nearly complete
destruction of the cell layers
The parameters of the test required the negative and reagent
controls to rate at grade 0, the positive control to rate at grade
3 or 4, and the test sample to rate at grade 2 or lower.
[0050] Under the conditions of the in vitro study, the 1.times.MEM
test extract showed no evidence of causing cell lysis or toxicity.
The reagent, positive and negative controls performed as
anticipated, and the test sample rated at less than grade 2,
thereby meeting the requirements of the test. In particular, each
of the test culture wells rated 0, indicating that alloys according
to embodiments of the present invention are not cytotoxic.
In Vivo Cytotoxicity Studies
[0051] The cytotoxicity of a glassy
Pd.sub.77.5Ag.sub.6Si.sub.9P.sub.7.5 test article was evaluated in
an in vivo biocompatibility study conducted by NAMSA (Northwood,
Ohio). The test article was implanted into muscle tissue of rabbit.
The muscle tissue was evaluated for evidence of irritation or
toxicity based on the requirements of the International
Organization for Standardization 10993: Biological Evaluation of
Medical Devices, part 6: Test for Local Effects after
Implantation.
[0052] A minimum of four sections of the test article per rabbit,
each approximately 1 mm.times.10 mm, were loaded into 14 gauge
needles. For each rabbit, a minimum of four negative control
samples were loaded into 14 gauge needles. 1 mm.times.10 mm
sections of high density polyethylene were used as the negative
control.
[0053] The rabbits were weighed and clipped free of fur over the
paravertebral muscles. An intramuscular injection of a combination
ketamine hydrochloride and xylazine (34 mg/kg+5 mg/kg) general
anesthetic was administered to each animal at a dose of 0.6 ml/kg.
Each rabbit was then injected subcutaneously with 0.02 mg/kg
buprenorphine. After the anesthetic had taken effect, the surgical
site was scrubbed with a germicidal soap, wiped with 70% isopropyl
alcohol, and painted with povidone iodine.
[0054] One incision was made on each side of the back through the
skin and parallel to the lumbar region of the vertebral column. A
stylet was placed in the hub of a loaded needle. The skin was moved
to the desired location and the needle was inserted through the
incision into the muscle at a 45.degree. angle. The needle was
withdrawn over the stylet, leaving the sample in the paravertebral
muscle. Four test article sections were implanted in the right
paravertebral muscle of each rabbit. Test article sections were
placed at appropriately spaced intervals. In the opposite muscle,
four negative control sections were similarly implanted. The skin
incisions were closed with tissue glue. After implantation, the
rabbits were monitored for recovery from the anesthetic, and
another dose of buprenorphine was administered a minimum of four
hours after the first dose. A day following implantation, a third
buprenorphine injection was administered.
[0055] The rabbits were observed daily for general health, and
their body weights were recorded prior to implantation and at
termination. At two weeks, the rabbits were weighed and then
euthanized by an intravenous injection of a sodium pentobarbitol
based drug. The paravertebral muscles were dissected free and fixed
in 10% neutral buffered formalin (NBF) to facilitate cutting. After
fixation, the muscles were methodically cut to locate test and
control article sites. All test and control article sites were
accounted for. Capsule formation or other signs of irritation were
scored using microscopically using low magnification and
macroscopically, and the scores were rated as in Table 5.
TABLE-US-00005 TABLE 5 Grade Condition 0 No capsule, no adverse
reaction (other than minimal hemorrhage) 1 Up to 0.5 mm capsule or
reaction area 2 0.6 to 1.0 mm capsule or reaction area 3 1.1 to 2.0
mm capsule or reaction area 4 >2.0 mm capsule or reaction
area
[0056] Macroscopically, there was no visible reaction at any test
or control site. Indeed, each of the test and control sites rated
0, indicating insignificant or nonexistent tissue contact
irritation.
[0057] Representative tissue implant sites (test and control) from
each rabbit were excised, allowing a sufficient area around the
site for proper histological preparation. These sections were
histologically processed (embedded, sectioned and stained in
hemotoxylin and eosin) for microscopic evaluation. The microscopic
evaluation of the representative implant sites was conducted to
further define any tissue response. The evaluation was conducted by
a qualified pathologist. The results of the microscopic evaluation
of the test and control sites are shown in Table 6.
TABLE-US-00006 TABLE 6 Rabbit 1: Rabbit 2: Rabbit 3: Rabbit 1:
Rabbit 2: Rabbit 3: Control Control Control Test Sites Test Sites
Test Sites Sites Sites Sites Inflammation 1 1 1 1 1 2
Polymorphonuclear Lymphocytes 1 1 1 1 1 1 Plasma Cells 0 0 0 0 0 0
Macrophages 1 2 1 2 2 2 Giant Cells 1 1 1 1 1 1 Necrosis 0 0 0 0 0
0 Neovascularization 0 0 0 0 0 0 Fibrosis 1 1 1 1 1 1 Fatty
Infiltrate 0 0 0 0 0 0 Traumatic Necrosis 0 0 0 1 1 0 Foreign
Debris 0 0 0 0 0 0
[0058] As shown in Table 6, the test sites performed as good as or
even better than the control. Accordingly, the test article was
classified as a nonirritant as compared to the negative control.
Given the results of the in vitro and in vivo studies, the alloys
according to embodiments of the present invention are not
cytotoxic, and are therefore suitable for use in biomedical
applications.
[0059] While the present invention has been illustrated and
described with reference to certain exemplary embodiments, those of
ordinary skill in the art understand that various modifications and
changes may be made to the described embodiments without departing
from the spirit and scope of the present invention as defined by
the following claims.
* * * * *